US20120040100A1 - Solution deposition planarization method - Google Patents
Solution deposition planarization method Download PDFInfo
- Publication number
- US20120040100A1 US20120040100A1 US13/168,093 US201113168093A US2012040100A1 US 20120040100 A1 US20120040100 A1 US 20120040100A1 US 201113168093 A US201113168093 A US 201113168093A US 2012040100 A1 US2012040100 A1 US 2012040100A1
- Authority
- US
- United States
- Prior art keywords
- solution
- substrate
- concentration
- rms
- oxide
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Abandoned
Links
- 238000000034 method Methods 0.000 title claims abstract description 52
- 230000008021 deposition Effects 0.000 title abstract description 18
- 239000000758 substrate Substances 0.000 claims abstract description 107
- SIWVEOZUMHYXCS-UHFFFAOYSA-N oxo(oxoyttriooxy)yttrium Chemical compound O=[Y]O[Y]=O SIWVEOZUMHYXCS-UHFFFAOYSA-N 0.000 claims abstract description 58
- 238000000576 coating method Methods 0.000 claims abstract description 54
- 230000003746 surface roughness Effects 0.000 claims abstract description 34
- 239000011248 coating agent Substances 0.000 claims abstract description 33
- 239000002243 precursor Substances 0.000 claims abstract description 29
- 238000010438 heat treatment Methods 0.000 claims abstract description 22
- 229910044991 metal oxide Inorganic materials 0.000 claims abstract description 22
- 150000004706 metal oxides Chemical class 0.000 claims abstract description 22
- 238000000151 deposition Methods 0.000 claims abstract description 20
- 239000002904 solvent Substances 0.000 claims abstract description 20
- 239000012702 metal oxide precursor Substances 0.000 claims abstract description 11
- NFSAPTWLWWYADB-UHFFFAOYSA-N n,n-dimethyl-1-phenylethane-1,2-diamine Chemical compound CN(C)C(CN)C1=CC=CC=C1 NFSAPTWLWWYADB-UHFFFAOYSA-N 0.000 claims description 12
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N Titan oxide Chemical compound O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 claims description 8
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 claims description 5
- 229910001404 rare earth metal oxide Inorganic materials 0.000 claims description 5
- 229910052727 yttrium Inorganic materials 0.000 claims description 5
- VWQVUPCCIRVNHF-UHFFFAOYSA-N yttrium atom Chemical compound [Y] VWQVUPCCIRVNHF-UHFFFAOYSA-N 0.000 claims description 5
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 claims description 4
- VQCBHWLJZDBHOS-UHFFFAOYSA-N erbium(iii) oxide Chemical compound O=[Er]O[Er]=O VQCBHWLJZDBHOS-UHFFFAOYSA-N 0.000 claims description 4
- 239000000203 mixture Substances 0.000 claims description 4
- RVTZCBVAJQQJTK-UHFFFAOYSA-N oxygen(2-);zirconium(4+) Chemical compound [O-2].[O-2].[Zr+4] RVTZCBVAJQQJTK-UHFFFAOYSA-N 0.000 claims description 3
- 229910000449 hafnium oxide Inorganic materials 0.000 claims description 2
- WIHZLLGSGQNAGK-UHFFFAOYSA-N hafnium(4+);oxygen(2-) Chemical compound [O-2].[O-2].[Hf+4] WIHZLLGSGQNAGK-UHFFFAOYSA-N 0.000 claims description 2
- OGIDPMRJRNCKJF-UHFFFAOYSA-N titanium oxide Inorganic materials [Ti]=O OGIDPMRJRNCKJF-UHFFFAOYSA-N 0.000 claims description 2
- 229910001928 zirconium oxide Inorganic materials 0.000 claims description 2
- 229910052814 silicon oxide Inorganic materials 0.000 claims 1
- 238000007735 ion beam assisted deposition Methods 0.000 abstract description 12
- 230000008901 benefit Effects 0.000 abstract description 6
- 238000004519 manufacturing process Methods 0.000 abstract description 3
- 239000010408 film Substances 0.000 description 11
- 229910021521 yttrium barium copper oxide Inorganic materials 0.000 description 9
- 238000005498 polishing Methods 0.000 description 7
- 239000002887 superconductor Substances 0.000 description 7
- 229910052751 metal Inorganic materials 0.000 description 6
- 239000002184 metal Substances 0.000 description 6
- MCMNRKCIXSYSNV-UHFFFAOYSA-N ZrO2 Inorganic materials O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 description 5
- 238000004630 atomic force microscopy Methods 0.000 description 5
- 239000007788 liquid Substances 0.000 description 5
- KFZMGEQAYNKOFK-UHFFFAOYSA-N Isopropanol Chemical compound CC(C)O KFZMGEQAYNKOFK-UHFFFAOYSA-N 0.000 description 4
- 229910052782 aluminium Inorganic materials 0.000 description 4
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 4
- 230000007423 decrease Effects 0.000 description 4
- 238000004549 pulsed laser deposition Methods 0.000 description 4
- OKKJLVBELUTLKV-UHFFFAOYSA-N Methanol Chemical compound OC OKKJLVBELUTLKV-UHFFFAOYSA-N 0.000 description 3
- 238000003917 TEM image Methods 0.000 description 3
- 229910000856 hastalloy Inorganic materials 0.000 description 3
- 238000002360 preparation method Methods 0.000 description 3
- RUDFQVOCFDJEEF-UHFFFAOYSA-N yttrium(III) oxide Inorganic materials [O-2].[O-2].[O-2].[Y+3].[Y+3] RUDFQVOCFDJEEF-UHFFFAOYSA-N 0.000 description 3
- 229910002370 SrTiO3 Inorganic materials 0.000 description 2
- 239000004020 conductor Substances 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 239000010432 diamond Substances 0.000 description 2
- 229910003460 diamond Inorganic materials 0.000 description 2
- 238000003618 dip coating Methods 0.000 description 2
- 238000001035 drying Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 229910001092 metal group alloy Inorganic materials 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 238000000197 pyrolysis Methods 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 239000010409 thin film Substances 0.000 description 2
- VXUYXOFXAQZZMF-UHFFFAOYSA-N titanium(IV) isopropoxide Chemical compound CC(C)O[Ti](OC(C)C)(OC(C)C)OC(C)C VXUYXOFXAQZZMF-UHFFFAOYSA-N 0.000 description 2
- 239000004215 Carbon black (E152) Substances 0.000 description 1
- 229910052581 Si3N4 Inorganic materials 0.000 description 1
- 238000002441 X-ray diffraction Methods 0.000 description 1
- 239000002253 acid Substances 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 238000000089 atomic force micrograph Methods 0.000 description 1
- 230000004888 barrier function Effects 0.000 description 1
- 230000005540 biological transmission Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- BSDOQSMQCZQLDV-UHFFFAOYSA-N butan-1-olate;zirconium(4+) Chemical compound [Zr+4].CCCC[O-].CCCC[O-].CCCC[O-].CCCC[O-] BSDOQSMQCZQLDV-UHFFFAOYSA-N 0.000 description 1
- 239000006227 byproduct Substances 0.000 description 1
- 239000000919 ceramic Substances 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 238000000224 chemical solution deposition Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000001419 dependent effect Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- ZBCBWPMODOFKDW-UHFFFAOYSA-N diethanolamine Chemical compound OCCNCCO ZBCBWPMODOFKDW-UHFFFAOYSA-N 0.000 description 1
- 230000003292 diminished effect Effects 0.000 description 1
- 230000009977 dual effect Effects 0.000 description 1
- 238000010894 electron beam technology Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 238000009499 grossing Methods 0.000 description 1
- 229930195733 hydrocarbon Natural products 0.000 description 1
- 150000002430 hydrocarbons Chemical class 0.000 description 1
- 238000011065 in-situ storage Methods 0.000 description 1
- 238000010884 ion-beam technique Methods 0.000 description 1
- 239000006193 liquid solution Substances 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 238000002488 metal-organic chemical vapour deposition Methods 0.000 description 1
- 229940087646 methanolamine Drugs 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 230000001590 oxidative effect Effects 0.000 description 1
- -1 polytetrafluoroethylene Polymers 0.000 description 1
- 229920001343 polytetrafluoroethylene Polymers 0.000 description 1
- 239000004810 polytetrafluoroethylene Substances 0.000 description 1
- 238000001314 profilometry Methods 0.000 description 1
- 239000010453 quartz Substances 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 229910052710 silicon Inorganic materials 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 239000000377 silicon dioxide Substances 0.000 description 1
- HQVNEWCFYHHQES-UHFFFAOYSA-N silicon nitride Chemical compound N12[Si]34N5[Si]62N3[Si]51N64 HQVNEWCFYHHQES-UHFFFAOYSA-N 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 229910001220 stainless steel Inorganic materials 0.000 description 1
- 239000007858 starting material Substances 0.000 description 1
- 238000000859 sublimation Methods 0.000 description 1
- 230000008022 sublimation Effects 0.000 description 1
- 239000004408 titanium dioxide Substances 0.000 description 1
- 231100000331 toxic Toxicity 0.000 description 1
- 230000002588 toxic effect Effects 0.000 description 1
- 239000002699 waste material Substances 0.000 description 1
- AIQRTHPXPDTMBQ-UHFFFAOYSA-K yttrium(3+);triacetate;tetrahydrate Chemical compound O.O.O.O.[Y+3].CC([O-])=O.CC([O-])=O.CC([O-])=O AIQRTHPXPDTMBQ-UHFFFAOYSA-K 0.000 description 1
Images
Classifications
-
- H—ELECTRICITY
- H10—SEMICONDUCTOR DEVICES; ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
- H10N—ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
- H10N60/00—Superconducting devices
- H10N60/01—Manufacture or treatment
- H10N60/0268—Manufacture or treatment of devices comprising copper oxide
- H10N60/0296—Processes for depositing or forming copper oxide superconductor layers
- H10N60/0576—Processes for depositing or forming copper oxide superconductor layers characterised by the substrate
- H10N60/0632—Intermediate layers, e.g. for growth control
Definitions
- the present invention relates generally to a solution deposition planarization method for providing a substrate with a very smooth surface.
- HTSCCs high temperature superconducting coated conductors
- Flexible substrates are light, and they offer other advantages of having large areas with small volumes, varying form factors, and a reduction of manufacturing costs when materials are processed roll to roll. Flexible substrates, however, may not have the surface smoothness needed for optimal performance.
- the preparation of practical, layered HTSCCs, for example, requires a very smooth surface for deposition of the superconductor.
- Ion-beam-assisted deposition (IBAD) texturing is used to create a biaxially textured (crystal-aligned) MgO layer for epitaxial growth of a highly aligned superconductor.
- the biaxially-textured MgO layer must be very thin, so an extremely smooth substrate is needed for the MgO layer.
- an inexpensive and fast process to produce smooth substrates for IBAD-MgO textured layers is needed.
- Mechanical polishing provides a smooth enough substrate surface but may not be practical for long lengths and/or large areas because mechanical polishing is expensive and time consuming.
- Electropolishing provides a fast process for preparing smooth substrates, but is limited to a few metal alloys, requires expensive starting materials, and generates toxic acid waste.
- An efficient and inexpensive process that transforms any rough substrate surface into a surface smooth enough for an IBAD-MgO textured layer is desirable.
- a surface roughness RMS of 1 nm or less (on a 5 ⁇ 5 ⁇ m scale) is required for high quality IBAD-MgO layer.
- An object of the invention is to provide an inexpensive and efficient process for substrate planarization that does not involve polishing but results in a surface that is smooth enough for an IBAD-MgO textured layer for subsequent deposition thereon of a superconductor.
- the present invention provides a process for planarizing a substrate.
- the process includes providing a substrate having a surface roughness of at least 3 nm RMS (root mean square).
- the substrate may have a much rougher surface, such as surface roughness of at least 20 nm RMS.
- the process also includes providing a first solution having a first concentration of yttrium oxide precursor in a solvent, and applying a coating of the solution to the rough surface.
- the coated substrate is heated under conditions sufficient to evaporate the solvent and convert the solution of yttrium oxide precursor to a layer of yttrium oxide on the substrate.
- the steps of applying a coating of the first solution and then heating are repeated to provide a plurality of layers of yttrium oxide, including a surface roughness less than 3 nm RMS but greater than 1 nm RMS (root mean square) on a 5 by 5 ⁇ m scale
- a second solution comprising a second concentration of yttrium precursor is also provided, the second concentration of the yttrium precursor being lower than the first concentration, and a coating of the second solution is applied on the layer of yttrium oxide.
- the now coated substrate is heated to evaporate the solvent and leave another layer of yttrium oxide on the substrate.
- the steps of applying a coating of the second solution and heating are repeated until a planarized substrate having plurality of layers of yttrium oxide deposited thereon is produced with a surface roughness less than 1 nm RMS.
- the above method above can be adapted by replacing yttrium oxide with another metal oxide.
- rare earth metal oxides may be deposited.
- the invention also includes a method for preparing a layered article.
- the method includes providing a substrate having a rough surface, providing a first solution comprising a first concentration of a metal oxide precursor in a solvent, applying a coating of the solution to the rough surface, heating the coated substrate under conditions sufficient to evaporate the solvent and convert the solution of metal oxide precursor to a layer of metal oxide on the substrate, repeating the steps of applying a coating of the first solution to the rough surface and heating, thereby forming a plurality of layers of metal oxide on the substrate.
- the method also includes providing a second solution comprising a second concentration of metal oxide precursor, the second concentration lower than the first concentration, applying a coating of the second solution on the layer of metal oxide, heating the coated substrate to evaporate the solvent and leave a layer of metal oxide on the substrate, and repeating the steps of applying a coating of the second solution and heating. Then a layer of IBAD-MgO is deposited on the metal oxide.
- FIG. 1 a shows a cross sectional view of a transmission electron micrograph (TEM) of a substrate coated with layers of yttrium oxide according to an embodiment.
- An IBAD-MgO layer is on the topmost yttrium oxide layer, a SrTiO 3 buffer layer on the IBAD-MgO layer, and YBCO superconductor layer is on top of the IBAD-MgO layer.
- FIG. 1 b is a higher magnification image of a portion of FIG. 1 a that shows individual layers of yttrium oxide in more detail.
- FIG. 2 shows a plot of RMS roughness as a function of the number of SDP coatings of an embodiment process using a 0.08 M solution of yttrium oxide precursor and a 0.04 M solution of the yttrium oxide precursor.
- FIG. 3 shows a plot of RMS roughness on a 5 ⁇ 5 micrometer area as a function of the number of SDP coatings for a 0.4 M solution of yttrium oxide precursor followed by a 0.08 M solution of the yttrium oxide precursor.
- FIG. 4 shows a plot of MgO texture as a function of the number of SDP coatings for two solutions. Solid symbols represent average out-of-plane texture and open symbols represent the in-plane texture.
- FIG. 5 a shows a plot of out of plane texture of IBAD-MgO vs. RMS roughness
- FIG. 5 b shows a ploy of in plane texture of IBAD-MgO vs. RMS roughness
- the IBAD-MgO is deposited on (i) a substrate planarized by SDP using a 0.4 M solution of yttrium acetate (black squares), (ii) a substrate planarized by SDP using a 0.08 M solution of yttrium acetate (gray squares), and (iii) a substrate planarized by SDP using a two-solution process wherein the first solution is 0.4 M yttrium acetate and the second solution is 0.08 M yttrium acetate (diamond), and (iv) a substrate planarized by mechanical polishing (open black circles).
- the mechanically polished samples data is from Matias et al. in Mater. Res. Soc. Symp. Proc., Barnes et al. editors, vol. 1001E, Warrendale, Pa., 2007, No. 100′-M04-02.
- the in plane texture is superior for the process involving the two solutions.
- the invention relates to a chemical solution deposition process to planarize a rough substrate surface efficiently, inexpensively, and in long lengths of substrate.
- layers are added that are smoother than the underlying rough substrate surface.
- the method is sometimes referred herein as Solution Deposition Planarization (SDP).
- SDP Solution Deposition Planarization
- the method has been shown to produce a surface roughness under 1 nm RMS starting with a substrate surface that is rougher by two orders of magnitude.
- the additional layers that planarize the substrate may also serve the dual purpose as an interdiffusion barrier.
- An aspect of this invention applies to the formation of a plurality of layers of yttrium oxide on a rough substrate surface to planarize the surface.
- This involves applying a coating of a first solution of yttrium oxide precursor to the rough surface.
- the precursor may be yttrium acetate, or some other yttrium containing precursor that converts to the oxide upon heating in an oxidizing environment.
- the coated substrate is heated under conditions sufficient to evaporate the solvent and convert the solution of yttrium oxide precursor to a layer of yttrium oxide on the substrate.
- These steps of applying a coating of the first solution and heating are repeated to provide a plurality of layers of yttrium oxide, the plurality with a surface roughness greater than 1 nm RMS.
- the surface roughness is preferably greater than 1 nm RMS but less than 5 nm RMS, or less than 4 nm RMS, or less than 3 nm RMS, or less than 2 nm RMS.
- a coating of a second solution is then applied to the topmost yttrium oxide layer, the second solution having a concentration of the yttrium oxide precursor that is less than the concentration of precursor in the first solution.
- the substrate is heated to evaporate the solvent and leave a second layer of yttrium oxide.
- the steps of applying a coating of the second solution and heating are repeated until a planarized substrate having plurality of layers of yttrium oxide deposited thereon is produced, the surface roughness now less than 1 nm RMS. It was found that when the concentration of yttrium oxide precursor is less for the second solution that the first, after forming a plurality of layers on the substrate, a surface roughness less than 1 nm RMS, less than 0.9 nm RMS, less than 0.8 nm RMS, less than 0.7 nm RMS, and even less than 0.6 nm RMS was achieved.
- a surface roughness between 0.6 nm RMS and 0.5 nm RMS was realized using this method when the concentration of the first solution was 0.4 M and the concentration of the second solution was 0.08 M when the yttrium oxide precursor was yttrium acetate.
- the method is applied to substrates with rough surfaces.
- the surface has a surface roughness of at least 20 nanometers (nm) RMS (root-mean-squared).
- the surface roughness is at least 30 nm RMS.
- the surface roughness is at least 40 nm RMS.
- the surface roughness is at least 50 nm RMS.
- the substrates may be metal substrates, ceramic substrates, or some other substrate having a rough surface.
- a metal or metal alloy such as a hastelloy may be a substrate.
- Silicon may be a substrate.
- a stainless steel may be a substrate.
- silica may be a substrate.
- alumina may be a substrate.
- silicon nitride may be a substrate.
- the substrates are flexible.
- the substrates should be long, at least 5 meters in length.
- Substrates having a length greater than 10 meters, greater than 25 meters, greater than 50 meters, greater than 100 meters, greater than 500 meters, greater than 1000 meters, greater than 5000 meters, greater than 10,000 meters, greater than 100,000 meters, greater than 250,000 meters, greater than 500,000 meters, greater than 1,000,000 meters, and so on, may be prepared using the present method.
- the invention does not involve polishing the substrate surface to eliminate surface roughness.
- the invention applies to substrates with rough surfaces that have not been subjected to mechanical polishing.
- the rough substrate surface prior to planarization is contoured with many peaks and valleys.
- the surface tension of the liquid planarizes the contoured surface resulting in thicker regions over the valleys and thinner regions over the peaks.
- the coating shrinks following the original substrate contours, with a decrease in roughness compared to the underlying substrate. By repeating the process a number of times, further reduction in roughness is obtained.
- Hastelloy C-276 metal tape 0.1 mm thick, was used as the substrate.
- the metal tape was 10 mm wide and about 5 meters long.
- the starting roughness was 33 nm RMS (50 micrometer scale). In another embodiment, the starting roughness was 21 nm (5 micrometer scale).
- Solution Deposition Planarization (SDP) coatings of yttria were done using dip coating in a continuous tape loop coater where the tape is dipped into a bath and then heated repeatedly.
- SDP Solution Deposition Planarization
- the dip coating bath included a submerged idler and the tape exits the free liquid surface away from the idler surface.
- the tape pull speed was 200 mm/min. The tape then entered a flow-controlled environment during the solvent drying stage to reduce turbulence.
- Solutions of 0.08 M and 0.40 M concentration were prepared by mixing yttrium (III) acetate tetrahydrate in a solvent of methanol and diethanolamine. The solutions were filtered using a 0.22 micrometer polytetrafluoroethylene syringe filter prior to use.
- Atomic force microscopy (AFM) and profilometry were used to measure the surface roughness and thin film thickness after every 5 SDP coatings.
- AFM scans were taken over 5 ⁇ 5 micrometer and 50 ⁇ 50 micrometer areas for 5 points and results were averaged.
- a second order flattening procedure was used to remove the background height in the AFM scans.
- IBAD-MgO a biaxially-textured layer of IBAD-MgO was applied. This procedure took place in a vacuum chamber. Tape samples from the SDP were spliced together. All the depositions were done in one IBAD pass and run. An ion beam of Ar at 1000 volts (V) was used for assist at 45° to the substrate normal. MgO was deposited by electron-beam sublimation at a rate of 0.45 nm/s. The MgO deposition time was 50 seconds. A homoepitaxial MgO layer of 150 nm was deposited in situ at a rate of 8 nanometers per second (nm/s) at approximately 500° C. Samples were analyzed by x-ray diffraction to determine the mosaic spreads.
- FIG. 1 a - b shows cross sectional transmission electron microscope (TEM) images of the Hastelloy tape after 15 SDP coatings of yttrium oxide, a layer of IBAD-MgO on the yttrium oxide, and YBCO on the IBAD-MgO layer.
- the planarization effect is noticeable, particularly in FIG. 1 b where the individual yttrium oxide layers are more clearly separated from each other.
- the SDP is tolerant of substrate defects as it encapsulates them and shows no sign of the defect at the interface with the IBAD-MgO layer.
- the RMS roughness over a 5 ⁇ 5 micrometer area was used to characterize the surfaces at each stage of deposition.
- the data after sequential coatings are shown in FIG. 2 for the two different solutions, 0.08 M and 0.4 M.
- the lower molarity solution has the slower planarization effect of the two solutions but its effectiveness persists for more passes than the higher molarity solution, which appears to saturate at a roughness of about 1.5 nm RMS.
- the two solutions yield approximately the same 5 micrometer roughness. However, 15 coatings of the 0.08 M solution is still rougher on this scale than only 5 coatings of the 0.4 M solution.
- t fin is the thickness that remains after pyrolysis and t init is the thickness of the last liquid state that retains a flat surface.
- the remaining roughness (R fin ) is then
- R fin R init s
- R init is the initial roughness. If there were no shrinkage, the resulting surface would be perfectly flat with no roughness. From this simple model, RMS roughness is R q wherein
- n is the number of coatings and R 0 is the initial RMS roughness of the substrate.
- R 0 is the initial RMS roughness of the substrate.
- the dashed lines in FIG. 2 are the fits to the initial slopes of the data for both solutions. For the 0.4 M solution, the data immediately fall off the fitted curve. For the 0.08 M solution, the data deviate from the fit at a higher number of coatings.
- the roughness of the SDP is limited by the residual roughness of each solution deposited film.
- AFM images indicate a granular structure to the films that is dependent on the film thickness.
- the ratio of the film thicknesses is approximately 5, which is close to the ratio of the molarities of the two solutions.
- the data show the residual roughness appears to be 1.5 nm or about 2.5% of the film thickness. The same relative fraction extrapolated to the 0.08 M solution would yield a residual roughness of about 0.4 nm.
- FIG. 4 is a plot of MgO texture as a function of the number of SDP coatings for the two solutions.
- Square symbols represent average out-of-plane texture and circles represent in-plane texture.
- the inset shows the out-of-plane texture as a function of RMS roughness together with the data taken from Matias et al. in Mater. Res. Soc. Symp. Proc., edited by Barnes et al., vol. 1001E, Warrendale, Pa., 2007, No. 1001-M04-02.
- the SDP prepared substrates were used for creating IBAD templates for superconducting coated conductors.
- a layer of YBa 2 Cu 3 O 7 (YBCO) of 1-3 micrometers in thickness was deposited on the IBAD template.
- YBCO deposition techniques were used successfully on these templates, including pulsed laser deposition (PLD), reactive coevaporation (RCE), and MOCVD.
- FIG. 1 a shows a 1.2 micrometer YBCO layer deposited by PLD on the IBAD/SDP template with a SrTiO3 buffer layer.
- the critical current, J c at 75K in self field (SF) was measured to be 2.85 MA/cm 2 .
- Another aspect of this invention relates to other benefits that are afforded by using a rough substrate and coating with a first solution and then with a second solution.
- a benefit relates to certain properties of an IBAD-MgO layer deposited on the topmost of the metal oxide layers. A surface roughness less than 1 nm RMS is not required.
- FIG. 5 a shows a plot of out of plane texture of IBAD-MgO vs. RMS roughness
- FIG. 5 b shows a plot of in plane texture of IBAD-MgO vs. RMS roughness.
- the plots compare the in plane texture of the IBAD-MgO layers deposited on a variety of surfaces.
- One of the surfaces is a mechanically polished substrate (open circles).
- Another surface is formed when a 0.4 M solution of yttrium acetate was used for solution deposition planarization (red squares), and the surface roughness RMS is shown on the x-axis.
- Another surface is formed when a 0.08 M solution of yttrium acetate was used for solution deposition planarization (gray squares), the surface roughness also shown on the x-axis.
- the in plane texture of the IBAD-MgO layer appears to be better for the lower molarity solution, and is best when two solutions (diamond), a first solution of 0.4 M, and a second solution of 0.08 M, are used.
- the plot also indicates that the lower molarities (0.08 M) provide a better in plane texture than the higher molarity coating (0.4 M). At higher surface roughness, the lower molarity coating is a good choice.
- the in plane texture for IBAD-MgO deposited on yttrium oxide was best for a process wherein a first solution of 0.4 M yttrium oxide precursor (yttrium acetate, for example) was used first, and then a second solution of lower molarity (0.08 M yttrium oxide precursor, yttrium acetate).
- the invention of solution deposition planarization may be used for smoothing substrates in long lengths with resulting RMS roughness less than 1 nm.
- these planarized substrates can be used directly for IBAD-MgO texturing with very high quality and then for deposition of very high Jc-cuprate superconductors.
- metal oxides besides yttrium oxide may be used instead of yttrium oxide, or in mixtures with yttrium oxide.
- These other metal oxides include aluminum oxide, titanium oxide, zirconium oxide, hafnium oxide, and rare earth metal oxides such as erbium oxide.
- a mixture of aluminum oxide with yttrium oxide may also be used.
- the invention has thus far been described using two solutions of two different concentrations.
- the method may be expanded by using three solutions of different molarities, wherein the first solution has a concentration greater than the second solution and the second solution has a concentration greater than the third solution.
- the method can be expanded to the use of four solutions wherein the first has the highest concentration of the metal oxide precursor, the second having a lower concentration than the first solution with the same precursor, the third solution having a concentration lower than the second, and the fourth a lower concentration than the third.
- This can be expanded for any number ‘n’ of solutions where the concentration decreases sequentially to the nth solution which has the lowest concentration of the metal oxide precursor.
- the invention also applies the preparation of metal oxynitride coatings.
- titanium dioxide and zirconium dioxide coatings were prepared to planarize unpolished aluminum plate to enable integrated electronics deposition atop the insulating TiO 2 or ZrO 2 top surface.
- Solutions of 0.15 M concentration and then 0.05M concentration (a) titanium isopropoxide in isopropanol or (b) zirconium butoxide in isopropanol were subsequently dip coated, using eight layers of each concentration, dried at 300° C. for 1 minute, and subsequently annealed in air at 450° C. for 10 minutes, atop 30 cm wide aluminum plates.
- the coatings reduced the initial 5 micron-scale roughness to less than 100 nm RMS after annealing.
- the TiO 2 or ZrO 2 coated aluminum was subsequently used as an insulating substrate for printed electronic circuit boards, in which the deposited conductive metal traces were then electrically insulated from the rough aluminum substrate via the planarization layers.
Landscapes
- Engineering & Computer Science (AREA)
- Manufacturing & Machinery (AREA)
- Superconductors And Manufacturing Methods Therefor (AREA)
Abstract
Description
- This application claims the benefit of U.S. Provisional Application No. 61/359,733, entitled “Substrates for Layered Superconductors,”, filed Jun. 29, 2010, which is incorporated by reference herein.
- This invention was made with government support under Contract No. DE-AC52-06NA25396 awarded by the U.S. Department of Energy. The government has certain rights in the invention.
- The present invention relates generally to a solution deposition planarization method for providing a substrate with a very smooth surface.
- Mechanically flexible substrates for thin films are growing in popularity for electronic devices such as displays, printed circuit boards, solar cells, batteries, and high temperature superconducting coated conductors (HTSCCs). Flexible substrates are light, and they offer other advantages of having large areas with small volumes, varying form factors, and a reduction of manufacturing costs when materials are processed roll to roll. Flexible substrates, however, may not have the surface smoothness needed for optimal performance. The preparation of practical, layered HTSCCs, for example, requires a very smooth surface for deposition of the superconductor. Ion-beam-assisted deposition (IBAD) texturing is used to create a biaxially textured (crystal-aligned) MgO layer for epitaxial growth of a highly aligned superconductor. The biaxially-textured MgO layer must be very thin, so an extremely smooth substrate is needed for the MgO layer. Thus, for practical implementation of HTSCCs, an inexpensive and fast process to produce smooth substrates for IBAD-MgO textured layers is needed. Mechanical polishing provides a smooth enough substrate surface but may not be practical for long lengths and/or large areas because mechanical polishing is expensive and time consuming. Electropolishing provides a fast process for preparing smooth substrates, but is limited to a few metal alloys, requires expensive starting materials, and generates toxic acid waste.
- An efficient and inexpensive process that transforms any rough substrate surface into a surface smooth enough for an IBAD-MgO textured layer is desirable. Generally, a surface roughness RMS of 1 nm or less (on a 5×5 μm scale) is required for high quality IBAD-MgO layer.
- An object of the invention is to provide an inexpensive and efficient process for substrate planarization that does not involve polishing but results in a surface that is smooth enough for an IBAD-MgO textured layer for subsequent deposition thereon of a superconductor.
- To achieve the foregoing and other objects, and in accordance with the purposes of the present invention, as embodied and broadly described herein, the present invention provides a process for planarizing a substrate. The process includes providing a substrate having a surface roughness of at least 3 nm RMS (root mean square). The substrate may have a much rougher surface, such as surface roughness of at least 20 nm RMS. The process also includes providing a first solution having a first concentration of yttrium oxide precursor in a solvent, and applying a coating of the solution to the rough surface. The coated substrate is heated under conditions sufficient to evaporate the solvent and convert the solution of yttrium oxide precursor to a layer of yttrium oxide on the substrate. The steps of applying a coating of the first solution and then heating are repeated to provide a plurality of layers of yttrium oxide, including a surface roughness less than 3 nm RMS but greater than 1 nm RMS (root mean square) on a 5 by 5 μm scale A second solution comprising a second concentration of yttrium precursor is also provided, the second concentration of the yttrium precursor being lower than the first concentration, and a coating of the second solution is applied on the layer of yttrium oxide. The now coated substrate is heated to evaporate the solvent and leave another layer of yttrium oxide on the substrate. The steps of applying a coating of the second solution and heating are repeated until a planarized substrate having plurality of layers of yttrium oxide deposited thereon is produced with a surface roughness less than 1 nm RMS.
- The above method above can be adapted by replacing yttrium oxide with another metal oxide. For example, rare earth metal oxides may be deposited.
- The invention also includes a method for preparing a layered article. The method includes providing a substrate having a rough surface, providing a first solution comprising a first concentration of a metal oxide precursor in a solvent, applying a coating of the solution to the rough surface, heating the coated substrate under conditions sufficient to evaporate the solvent and convert the solution of metal oxide precursor to a layer of metal oxide on the substrate, repeating the steps of applying a coating of the first solution to the rough surface and heating, thereby forming a plurality of layers of metal oxide on the substrate. The method also includes providing a second solution comprising a second concentration of metal oxide precursor, the second concentration lower than the first concentration, applying a coating of the second solution on the layer of metal oxide, heating the coated substrate to evaporate the solvent and leave a layer of metal oxide on the substrate, and repeating the steps of applying a coating of the second solution and heating. Then a layer of IBAD-MgO is deposited on the metal oxide.
- The accompanying drawings, which are incorporated in and form a part of the specification, illustrate the embodiments of the present invention and, together with the description, serve to explain the principles of the invention. In the drawings:
-
FIG. 1 a shows a cross sectional view of a transmission electron micrograph (TEM) of a substrate coated with layers of yttrium oxide according to an embodiment. An IBAD-MgO layer is on the topmost yttrium oxide layer, a SrTiO3 buffer layer on the IBAD-MgO layer, and YBCO superconductor layer is on top of the IBAD-MgO layer.FIG. 1 b is a higher magnification image of a portion ofFIG. 1 a that shows individual layers of yttrium oxide in more detail. -
FIG. 2 shows a plot of RMS roughness as a function of the number of SDP coatings of an embodiment process using a 0.08 M solution of yttrium oxide precursor and a 0.04 M solution of the yttrium oxide precursor. -
FIG. 3 shows a plot of RMS roughness on a 5×5 micrometer area as a function of the number of SDP coatings for a 0.4 M solution of yttrium oxide precursor followed by a 0.08 M solution of the yttrium oxide precursor. -
FIG. 4 shows a plot of MgO texture as a function of the number of SDP coatings for two solutions. Solid symbols represent average out-of-plane texture and open symbols represent the in-plane texture. -
FIG. 5 a shows a plot of out of plane texture of IBAD-MgO vs. RMS roughness, andFIG. 5 b shows a ploy of in plane texture of IBAD-MgO vs. RMS roughness, wherein for both FIGURES the IBAD-MgO is deposited on (i) a substrate planarized by SDP using a 0.4 M solution of yttrium acetate (black squares), (ii) a substrate planarized by SDP using a 0.08 M solution of yttrium acetate (gray squares), and (iii) a substrate planarized by SDP using a two-solution process wherein the first solution is 0.4 M yttrium acetate and the second solution is 0.08 M yttrium acetate (diamond), and (iv) a substrate planarized by mechanical polishing (open black circles). The mechanically polished samples data is from Matias et al. in Mater. Res. Soc. Symp. Proc., Barnes et al. editors, vol. 1001E, Warrendale, Pa., 2007, No. 100′-M04-02. The in plane texture is superior for the process involving the two solutions. - The invention relates to a chemical solution deposition process to planarize a rough substrate surface efficiently, inexpensively, and in long lengths of substrate. Instead of removing material to planarize a substrate having a rough surface, as a polishing method does, layers are added that are smoother than the underlying rough substrate surface. The method is sometimes referred herein as Solution Deposition Planarization (SDP). The method has been shown to produce a surface roughness under 1 nm RMS starting with a substrate surface that is rougher by two orders of magnitude. For the preparation of layered structures that support IBAD-MgO, the additional layers that planarize the substrate may also serve the dual purpose as an interdiffusion barrier.
- An aspect of this invention applies to the formation of a plurality of layers of yttrium oxide on a rough substrate surface to planarize the surface. This involves applying a coating of a first solution of yttrium oxide precursor to the rough surface. The precursor may be yttrium acetate, or some other yttrium containing precursor that converts to the oxide upon heating in an oxidizing environment. The coated substrate is heated under conditions sufficient to evaporate the solvent and convert the solution of yttrium oxide precursor to a layer of yttrium oxide on the substrate. These steps of applying a coating of the first solution and heating are repeated to provide a plurality of layers of yttrium oxide, the plurality with a surface roughness greater than 1 nm RMS. At this stage, the surface roughness is preferably greater than 1 nm RMS but less than 5 nm RMS, or less than 4 nm RMS, or less than 3 nm RMS, or less than 2 nm RMS. Once this level of roughness is achieved, a coating of a second solution is then applied to the topmost yttrium oxide layer, the second solution having a concentration of the yttrium oxide precursor that is less than the concentration of precursor in the first solution. The substrate is heated to evaporate the solvent and leave a second layer of yttrium oxide. The steps of applying a coating of the second solution and heating are repeated until a planarized substrate having plurality of layers of yttrium oxide deposited thereon is produced, the surface roughness now less than 1 nm RMS. It was found that when the concentration of yttrium oxide precursor is less for the second solution that the first, after forming a plurality of layers on the substrate, a surface roughness less than 1 nm RMS, less than 0.9 nm RMS, less than 0.8 nm RMS, less than 0.7 nm RMS, and even less than 0.6 nm RMS was achieved. In an embodiment, a surface roughness between 0.6 nm RMS and 0.5 nm RMS was realized using this method when the concentration of the first solution was 0.4 M and the concentration of the second solution was 0.08 M when the yttrium oxide precursor was yttrium acetate.
- The method is applied to substrates with rough surfaces. By rough, the surface has a surface roughness of at least 20 nanometers (nm) RMS (root-mean-squared). In some embodiments, the surface roughness is at least 30 nm RMS. In some embodiments, the surface roughness is at least 40 nm RMS. In other embodiments, the surface roughness is at least 50 nm RMS.
- The substrates may be metal substrates, ceramic substrates, or some other substrate having a rough surface. In an embodiment, a metal or metal alloy, such as a hastelloy may be a substrate. Silicon may be a substrate. In an embodiment, a stainless steel may be a substrate. In another embodiment, silica may be a substrate. In another embodiment, alumina may be a substrate. In another embodiment, silicon nitride may be a substrate.
- The substrates are flexible. For the purposes of preparing flexible layered coated superconductors, the substrates should be long, at least 5 meters in length. Substrates having a length greater than 10 meters, greater than 25 meters, greater than 50 meters, greater than 100 meters, greater than 500 meters, greater than 1000 meters, greater than 5000 meters, greater than 10,000 meters, greater than 100,000 meters, greater than 250,000 meters, greater than 500,000 meters, greater than 1,000,000 meters, and so on, may be prepared using the present method. There is in fact, no limit to the length of the substrate having a rough surface that can be used with the present method.
- It should be understood that the invention does not involve polishing the substrate surface to eliminate surface roughness. The invention applies to substrates with rough surfaces that have not been subjected to mechanical polishing.
- The rough substrate surface prior to planarization is contoured with many peaks and valleys. Upon coating with a liquid solution, the surface tension of the liquid planarizes the contoured surface resulting in thicker regions over the valleys and thinner regions over the peaks. After drying and pyrolysis, the coating shrinks following the original substrate contours, with a decrease in roughness compared to the underlying substrate. By repeating the process a number of times, further reduction in roughness is obtained.
- In an embodiment, Hastelloy C-276 metal tape, 0.1 mm thick, was used as the substrate. In an embodiment, the metal tape was 10 mm wide and about 5 meters long. In an embodiment the starting roughness was 33 nm RMS (50 micrometer scale). In another embodiment, the starting roughness was 21 nm (5 micrometer scale).
- Solution Deposition Planarization (SDP) coatings of yttria (Y2O3) were done using dip coating in a continuous tape loop coater where the tape is dipped into a bath and then heated repeatedly. A diagram of the apparatus can be found in FIG. 3 of Hänisch et al. entitled “Stacks of YBCO Films Using Multiple IBAD Templates,” IEEE Transactions on Applied Superconductivity, June 2007, vol. 17, no. 2, pp. 3577-3580, hereby incorporated by reference. The dip coating bath included a submerged idler and the tape exits the free liquid surface away from the idler surface. The tape pull speed was 200 mm/min. The tape then entered a flow-controlled environment during the solvent drying stage to reduce turbulence. Subsequently, yttria conversion and hydrocarbon oxidation took place in a 22 mm OD, 610 mm long, quartz tube at a temperature of 515±10° C. Dry compressed air flow at 11.8 L/min ensured sufficient oxidation and removal of byproducts within the tube.
- Multiple passes were performed by continuous operation of the coater. Solutions of 0.08 M and 0.40 M concentration were prepared by mixing yttrium (III) acetate tetrahydrate in a solvent of methanol and diethanolamine. The solutions were filtered using a 0.22 micrometer polytetrafluoroethylene syringe filter prior to use.
- Atomic force microscopy (AFM) and profilometry were used to measure the surface roughness and thin film thickness after every 5 SDP coatings. AFM scans were taken over 5×5 micrometer and 50×50 micrometer areas for 5 points and results were averaged. A second order flattening procedure was used to remove the background height in the AFM scans.
- Following SDP, a biaxially-textured layer of IBAD-MgO was applied. This procedure took place in a vacuum chamber. Tape samples from the SDP were spliced together. All the depositions were done in one IBAD pass and run. An ion beam of Ar at 1000 volts (V) was used for assist at 45° to the substrate normal. MgO was deposited by electron-beam sublimation at a rate of 0.45 nm/s. The MgO deposition time was 50 seconds. A homoepitaxial MgO layer of 150 nm was deposited in situ at a rate of 8 nanometers per second (nm/s) at approximately 500° C. Samples were analyzed by x-ray diffraction to determine the mosaic spreads. The procedure used for the MgO deposition has been described in a paper by Matias et al. entitled “Very Fast Biaxial Texture Evolution Using High Rate Ion-Beam-Assisted Deposition of MgO,” J. Mater. Res., January 2009, vol. 24, p. 125-129, incorporated by reference herein.
-
FIG. 1 a-b shows cross sectional transmission electron microscope (TEM) images of the Hastelloy tape after 15 SDP coatings of yttrium oxide, a layer of IBAD-MgO on the yttrium oxide, and YBCO on the IBAD-MgO layer. The planarization effect is noticeable, particularly inFIG. 1 b where the individual yttrium oxide layers are more clearly separated from each other. Furthermore, particularly inFIG. 1 b, one can see that the SDP is tolerant of substrate defects as it encapsulates them and shows no sign of the defect at the interface with the IBAD-MgO layer. - The RMS roughness over a 5×5 micrometer area was used to characterize the surfaces at each stage of deposition. The data after sequential coatings are shown in
FIG. 2 for the two different solutions, 0.08 M and 0.4 M. The lower molarity solution has the slower planarization effect of the two solutions but its effectiveness persists for more passes than the higher molarity solution, which appears to saturate at a roughness of about 1.5 nm RMS. At 25 coatings, the two solutions yield approximately the same 5 micrometer roughness. However, 15 coatings of the 0.08 M solution is still rougher on this scale than only 5 coatings of the 0.4 M solution. - The results were analyzed using a simple model for the decrease in roughness resulting from the amount of shrinkage in each coating. The liquid layer is assumed to be perfectly flat. As the liquid evaporates and the coating shrinks into a solid and then converts to the oxide film, the films regain some of the original roughness, but diminished in magnitude. The remaining roughness can be modeled from the shrinkage of the film. Shrinkage (s) is defined as follows:
-
s=1−t fin /t init - where tfin is the thickness that remains after pyrolysis and tinit is the thickness of the last liquid state that retains a flat surface. The remaining roughness (Rfin) is then
-
Rfin=Rinits, - where Rinit is the initial roughness. If there were no shrinkage, the resulting surface would be perfectly flat with no roughness. From this simple model, RMS roughness is Rq wherein
-
Rq=R0sn - where n is the number of coatings and R0 is the initial RMS roughness of the substrate. The dashed lines in
FIG. 2 are the fits to the initial slopes of the data for both solutions. For the 0.4 M solution, the data immediately fall off the fitted curve. For the 0.08 M solution, the data deviate from the fit at a higher number of coatings. - We postulate that the roughness of the SDP is limited by the residual roughness of each solution deposited film. AFM images indicate a granular structure to the films that is dependent on the film thickness. For the 0.08 M solution film thickness was measured to be 12 nm±2 nm and for the 0.4 M solution 62 nm±5 nm. The ratio of the film thicknesses is approximately 5, which is close to the ratio of the molarities of the two solutions. For the 0.4 M solution SDP, the data show the residual roughness appears to be 1.5 nm or about 2.5% of the film thickness. The same relative fraction extrapolated to the 0.08 M solution would yield a residual roughness of about 0.4 nm. In an attempt to verify our prediction, a second set of experiments was performed where we first coated with the 0.4 M solution and then with the 0.08 solution. Results are shown in
FIG. 3 . After 15 coatings with the 0.4 M solution of yttrium oxide precursor, the RMS roughness was reduced to 2.5 nm. Further coatings with the 0.08 solution of yttrium oxide precursor reduced the roughness to about 0.5 nm where it saturated. - IBAD texture measurements were performed on the series of SDP coatings with the two different molarity solutions. The resulting MgO in-plane and out-of-plane texture data are shown in
FIG. 4 , which is a plot of MgO texture as a function of the number of SDP coatings for the two solutions. Square symbols represent average out-of-plane texture and circles represent in-plane texture. The inset shows the out-of-plane texture as a function of RMS roughness together with the data taken from Matias et al. in Mater. Res. Soc. Symp. Proc., edited by Barnes et al., vol. 1001E, Warrendale, Pa., 2007, No. 1001-M04-02. A decrease in the FWHM for the mosaic spreads as a function of SDP coatings. The out of plane texture (lower part of the graph) correlates well with the RMS roughness as measured by the AFM on a 5×5 micrometer area. The inset ofFIG. 4 plots these out-of-plane data versus roughness with the previously published data for mechanically polished samples described in Matias et al. in Mater. Res. Soc. Symp. Proc., edited by Barnes et al., vol. 1001E, Warrendale, Pa., 2007, No. 1001-M04-02. This agreement was good, but the in-plane texture did not correlate well with only the roughness values. From this data, the 0.08 M solution had better in-plane texture than the 0.04 M solution, even though the roughness numbers were reversed (seeFIG. 2 ). - The SDP prepared substrates were used for creating IBAD templates for superconducting coated conductors. In an embodiment, a layer of YBa2Cu3O7 (YBCO) of 1-3 micrometers in thickness was deposited on the IBAD template. A number of different YBCO deposition techniques were used successfully on these templates, including pulsed laser deposition (PLD), reactive coevaporation (RCE), and MOCVD.
FIG. 1 a shows a 1.2 micrometer YBCO layer deposited by PLD on the IBAD/SDP template with a SrTiO3 buffer layer. For this sample, the critical current, Jc, at 75K in self field (SF) was measured to be 2.85 MA/cm2. For comparison, a RCE YBCO film of 1 micrometer was deposited on an IBAD/SDP template and the Jc at 75K (SF) was 4 MA/cm2 without a buffer layer. These Jc values match or exceed the best undoped YBCO samples made by PLD on single crystal substrates (see: Foltyn et al., Nat. Mater., 2007, vol. 6, p. 631). - Another aspect of this invention relates to other benefits that are afforded by using a rough substrate and coating with a first solution and then with a second solution. A benefit relates to certain properties of an IBAD-MgO layer deposited on the topmost of the metal oxide layers. A surface roughness less than 1 nm RMS is not required.
- Certain benefits in grain alignment were found when IBAD-MgO was deposited on yttrium oxide, which was applied by solution deposition planarization on a rough substrate, wherein a two solution process was used for deposition of the yttrium oxide. In particular, it was found that the in-plane texture of an IBAD-MgO layer deposited on the topmost layer formed from a coating process using two solutions of yttrium oxide was superior compared to a process involving the use of only one 0.4 M solution.
FIG. 5 a shows a plot of out of plane texture of IBAD-MgO vs. RMS roughness, andFIG. 5 b shows a plot of in plane texture of IBAD-MgO vs. RMS roughness. The plots compare the in plane texture of the IBAD-MgO layers deposited on a variety of surfaces. One of the surfaces is a mechanically polished substrate (open circles). Another surface is formed when a 0.4 M solution of yttrium acetate was used for solution deposition planarization (red squares), and the surface roughness RMS is shown on the x-axis. Another surface is formed when a 0.08 M solution of yttrium acetate was used for solution deposition planarization (gray squares), the surface roughness also shown on the x-axis. The in plane texture of the IBAD-MgO layer appears to be better for the lower molarity solution, and is best when two solutions (diamond), a first solution of 0.4 M, and a second solution of 0.08 M, are used. The plot also indicates that the lower molarities (0.08 M) provide a better in plane texture than the higher molarity coating (0.4 M). At higher surface roughness, the lower molarity coating is a good choice. - Thus, the in plane texture for IBAD-MgO deposited on yttrium oxide was best for a process wherein a first solution of 0.4 M yttrium oxide precursor (yttrium acetate, for example) was used first, and then a second solution of lower molarity (0.08 M yttrium oxide precursor, yttrium acetate).
- In summary, the invention of solution deposition planarization may be used for smoothing substrates in long lengths with resulting RMS roughness less than 1 nm. With the appropriate solution deposited layers, these planarized substrates can be used directly for IBAD-MgO texturing with very high quality and then for deposition of very high Jc-cuprate superconductors.
- Although the present invention has been described with reference to specific details, it is not intended that such details should be regarded as limitations upon the scope of the invention, except as and to the extent that they are included in the accompanying claims. For example, metal oxides besides yttrium oxide may be used instead of yttrium oxide, or in mixtures with yttrium oxide. These other metal oxides include aluminum oxide, titanium oxide, zirconium oxide, hafnium oxide, and rare earth metal oxides such as erbium oxide. A mixture of aluminum oxide with yttrium oxide may also be used. In addition, the invention has thus far been described using two solutions of two different concentrations. It should be understood that the method may be expanded by using three solutions of different molarities, wherein the first solution has a concentration greater than the second solution and the second solution has a concentration greater than the third solution. The method can be expanded to the use of four solutions wherein the first has the highest concentration of the metal oxide precursor, the second having a lower concentration than the first solution with the same precursor, the third solution having a concentration lower than the second, and the fourth a lower concentration than the third. This can be expanded for any number ‘n’ of solutions where the concentration decreases sequentially to the nth solution which has the lowest concentration of the metal oxide precursor. The invention also applies the preparation of metal oxynitride coatings.
- In another embodiment, titanium dioxide and zirconium dioxide coatings were prepared to planarize unpolished aluminum plate to enable integrated electronics deposition atop the insulating TiO2 or ZrO2 top surface. Solutions of 0.15 M concentration and then 0.05M concentration (a) titanium isopropoxide in isopropanol or (b) zirconium butoxide in isopropanol were subsequently dip coated, using eight layers of each concentration, dried at 300° C. for 1 minute, and subsequently annealed in air at 450° C. for 10 minutes, atop 30 cm wide aluminum plates. The coatings reduced the initial 5 micron-scale roughness to less than 100 nm RMS after annealing. The TiO2 or ZrO2 coated aluminum was subsequently used as an insulating substrate for printed electronic circuit boards, in which the deposited conductive metal traces were then electrically insulated from the rough aluminum substrate via the planarization layers.
Claims (19)
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US13/168,093 US20120040100A1 (en) | 2010-06-29 | 2011-06-24 | Solution deposition planarization method |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US35973310P | 2010-06-29 | 2010-06-29 | |
US13/168,093 US20120040100A1 (en) | 2010-06-29 | 2011-06-24 | Solution deposition planarization method |
Publications (1)
Publication Number | Publication Date |
---|---|
US20120040100A1 true US20120040100A1 (en) | 2012-02-16 |
Family
ID=45441502
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US13/168,093 Abandoned US20120040100A1 (en) | 2010-06-29 | 2011-06-24 | Solution deposition planarization method |
Country Status (2)
Country | Link |
---|---|
US (1) | US20120040100A1 (en) |
WO (1) | WO2012005977A1 (en) |
Cited By (16)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2013155220A1 (en) * | 2012-04-13 | 2013-10-17 | Applied Materials, Inc. | Ceramic coated ring and process for applying ceramic coating |
DE102013214447B3 (en) * | 2013-07-24 | 2014-11-20 | Bruker Hts Gmbh | Band-shaped, superconducting element with improved self-protection in quenching |
US20140363582A1 (en) * | 2013-06-11 | 2014-12-11 | Korea Electrotechnology Research Institute | Method of preparing yttria solution for buffer layer of substrate |
US9034199B2 (en) | 2012-02-21 | 2015-05-19 | Applied Materials, Inc. | Ceramic article with reduced surface defect density and process for producing a ceramic article |
US9090046B2 (en) | 2012-04-16 | 2015-07-28 | Applied Materials, Inc. | Ceramic coated article and process for applying ceramic coating |
US9212099B2 (en) | 2012-02-22 | 2015-12-15 | Applied Materials, Inc. | Heat treated ceramic substrate having ceramic coating and heat treatment for coated ceramics |
US9343289B2 (en) | 2012-07-27 | 2016-05-17 | Applied Materials, Inc. | Chemistry compatible coating material for advanced device on-wafer particle performance |
US9394615B2 (en) | 2012-04-27 | 2016-07-19 | Applied Materials, Inc. | Plasma resistant ceramic coated conductive article |
US9604249B2 (en) | 2012-07-26 | 2017-03-28 | Applied Materials, Inc. | Innovative top-coat approach for advanced device on-wafer particle performance |
US9735318B2 (en) | 2015-02-10 | 2017-08-15 | iBeam Materials, Inc. | Epitaxial hexagonal materials on IBAD-textured substrates |
US9865434B2 (en) | 2013-06-05 | 2018-01-09 | Applied Materials, Inc. | Rare-earth oxide based erosion resistant coatings for semiconductor application |
US10160660B1 (en) | 2014-05-28 | 2018-12-25 | National Technology & Engineering Solutions Of Sandia, Llc | Vanadium oxide for infrared coatings and methods thereof |
US10243105B2 (en) | 2015-02-10 | 2019-03-26 | iBeam Materials, Inc. | Group-III nitride devices and systems on IBAD-textured substrates |
US10501843B2 (en) | 2013-06-20 | 2019-12-10 | Applied Materials, Inc. | Plasma erosion resistant rare-earth oxide based thin film coatings |
US11047035B2 (en) | 2018-02-23 | 2021-06-29 | Applied Materials, Inc. | Protective yttria coating for semiconductor equipment parts |
USRE49869E1 (en) | 2015-02-10 | 2024-03-12 | iBeam Materials, Inc. | Group-III nitride devices and systems on IBAD-textured substrates |
Families Citing this family (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN102955595B (en) * | 2011-08-21 | 2016-05-25 | 宸鸿科技(厦门)有限公司 | Sensing method of touch control and device |
BE1020692A3 (en) | 2012-05-16 | 2014-03-04 | Prayon Sa | METHOD FOR MANUFACTURING COMPOSITE MATERIAL |
CN104233297B (en) * | 2014-09-17 | 2016-11-30 | 上海大学 | The quick leveling method of high-temperature superconductor band substrate |
CN113476157A (en) * | 2021-07-08 | 2021-10-08 | 上海森艺医疗科技有限公司 | Zirconia dental crown and preparation method thereof |
Family Cites Families (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US5259885A (en) * | 1991-04-03 | 1993-11-09 | American Superconductor Corporation | Process for making ceramic/metal and ceramic/ceramic laminates by oxidation of a metal precursor |
US5470820A (en) * | 1991-05-06 | 1995-11-28 | Hauser Chemical Research, Inc. | Electroplating of superconductor elements |
US20040248014A1 (en) * | 2003-01-30 | 2004-12-09 | West Robert C. | Electrolyte including polysiloxane with cyclic carbonate groups |
US7510641B2 (en) * | 2003-07-21 | 2009-03-31 | Los Alamos National Security, Llc | High current density electropolishing in the preparation of highly smooth substrate tapes for coated conductors |
EP1805817B1 (en) * | 2004-10-01 | 2016-11-16 | American Superconductor Corporation | Thick superconductor films with improved performance |
-
2011
- 2011-06-24 US US13/168,093 patent/US20120040100A1/en not_active Abandoned
- 2011-06-24 WO PCT/US2011/041753 patent/WO2012005977A1/en active Application Filing
Non-Patent Citations (3)
Title |
---|
Guillen et al "Leveling Effect of Sol-gel SiO2 Coatings onto Metallic Foil Substrates" Surface and Coatings Technology 138 (2001) 205-210. * |
Hu et al. "The Surface Morphology of Ba0.65Sr0.35TiO3 Thin Film by Sol-Gel Method" Integrated Ferroelectronics, 72, 1-11, 2005. * |
Lu et al "Development of textured MgO Templates on Nonmetallic Flexible Ceraflex" Applied Physics Letters 89, 132505-1-132505-3 (2006). * |
Cited By (26)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US10336656B2 (en) | 2012-02-21 | 2019-07-02 | Applied Materials, Inc. | Ceramic article with reduced surface defect density |
US9034199B2 (en) | 2012-02-21 | 2015-05-19 | Applied Materials, Inc. | Ceramic article with reduced surface defect density and process for producing a ceramic article |
US11279661B2 (en) | 2012-02-22 | 2022-03-22 | Applied Materials, Inc. | Heat treated ceramic substrate having ceramic coating |
US10364197B2 (en) | 2012-02-22 | 2019-07-30 | Applied Materials, Inc. | Heat treated ceramic substrate having ceramic coating |
US9212099B2 (en) | 2012-02-22 | 2015-12-15 | Applied Materials, Inc. | Heat treated ceramic substrate having ceramic coating and heat treatment for coated ceramics |
WO2013155220A1 (en) * | 2012-04-13 | 2013-10-17 | Applied Materials, Inc. | Ceramic coated ring and process for applying ceramic coating |
US9090046B2 (en) | 2012-04-16 | 2015-07-28 | Applied Materials, Inc. | Ceramic coated article and process for applying ceramic coating |
US9394615B2 (en) | 2012-04-27 | 2016-07-19 | Applied Materials, Inc. | Plasma resistant ceramic coated conductive article |
US9604249B2 (en) | 2012-07-26 | 2017-03-28 | Applied Materials, Inc. | Innovative top-coat approach for advanced device on-wafer particle performance |
US9343289B2 (en) | 2012-07-27 | 2016-05-17 | Applied Materials, Inc. | Chemistry compatible coating material for advanced device on-wafer particle performance |
US9865434B2 (en) | 2013-06-05 | 2018-01-09 | Applied Materials, Inc. | Rare-earth oxide based erosion resistant coatings for semiconductor application |
US10734202B2 (en) | 2013-06-05 | 2020-08-04 | Applied Materials, Inc. | Rare-earth oxide based erosion resistant coatings for semiconductor application |
US20140363582A1 (en) * | 2013-06-11 | 2014-12-11 | Korea Electrotechnology Research Institute | Method of preparing yttria solution for buffer layer of substrate |
US11680308B2 (en) | 2013-06-20 | 2023-06-20 | Applied Materials, Inc. | Plasma erosion resistant rare-earth oxide based thin film coatings |
US10501843B2 (en) | 2013-06-20 | 2019-12-10 | Applied Materials, Inc. | Plasma erosion resistant rare-earth oxide based thin film coatings |
US11053581B2 (en) | 2013-06-20 | 2021-07-06 | Applied Materials, Inc. | Plasma erosion resistant rare-earth oxide based thin film coatings |
US9640979B2 (en) | 2013-07-24 | 2017-05-02 | Bruker H I S GmbH | Band-shaped superconducting element with improved self-protection in case of quenching |
DE102013214447B3 (en) * | 2013-07-24 | 2014-11-20 | Bruker Hts Gmbh | Band-shaped, superconducting element with improved self-protection in quenching |
EP2830107A1 (en) | 2013-07-24 | 2015-01-28 | Bruker HTS GmbH | Tape-shaped, superconducting element with improved self-protection fields in case of quenching |
US10889506B2 (en) | 2014-05-28 | 2021-01-12 | National Technology & Engineering Solutions Of Sandia, Llc | Vanadium oxide for infrared coatings and methods thereof |
US10160660B1 (en) | 2014-05-28 | 2018-12-25 | National Technology & Engineering Solutions Of Sandia, Llc | Vanadium oxide for infrared coatings and methods thereof |
US9735318B2 (en) | 2015-02-10 | 2017-08-15 | iBeam Materials, Inc. | Epitaxial hexagonal materials on IBAD-textured substrates |
US10546976B2 (en) | 2015-02-10 | 2020-01-28 | iBeam Materials, Inc. | Group-III nitride devices and systems on IBAD-textured substrates |
US10243105B2 (en) | 2015-02-10 | 2019-03-26 | iBeam Materials, Inc. | Group-III nitride devices and systems on IBAD-textured substrates |
USRE49869E1 (en) | 2015-02-10 | 2024-03-12 | iBeam Materials, Inc. | Group-III nitride devices and systems on IBAD-textured substrates |
US11047035B2 (en) | 2018-02-23 | 2021-06-29 | Applied Materials, Inc. | Protective yttria coating for semiconductor equipment parts |
Also Published As
Publication number | Publication date |
---|---|
WO2012005977A1 (en) | 2012-01-12 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
US20120040100A1 (en) | Solution deposition planarization method | |
US10446294B2 (en) | Coated conductor high temperature superconductor carrying high critical current under magnetic field by intrinsic pinning centers, and methods of manufacture of same | |
Sheehan et al. | Solution deposition planarization of long-length flexible substrates | |
US6383989B2 (en) | Architecture for high critical current superconducting tapes | |
RU2384907C1 (en) | Superconducting thin-film material and method of making said material | |
RU2332737C2 (en) | Superconductive wire and method of its manufacturing | |
US20120028810A1 (en) | Method for depositing oxide thin films on textured and curved metal surfaces | |
JP5799081B2 (en) | Thick oxide film with single layer coating | |
WO2006082747A1 (en) | Superconducting thin film material, superconducting wire rod and methods for manufacturing such superconducting thin film material and superconducting wire rod | |
Cai et al. | Completely etch-free fabrication of multifilamentary coated conductor using inkjet printing and electrodeposition | |
Qiao et al. | Scale up of coated conductor substrate process by reel-to-reel planarization of amorphous oxide layers | |
DE60031784T2 (en) | IMPROVED HIGH TEMPERATURE SUPER PLATE COATED ELEMENTS | |
Haugan et al. | Flux pinning of Y-Ba-Cu-O films doped with BaZrO 3 nanoparticles by multilayer and single target methods | |
Narayanan et al. | Aqueous chemical solution deposition of lanthanum zirconate and related lattice-matched single buffer layers suitable for YBCO coated conductors: A review | |
Zhou et al. | Highly efficient colloid–solution deposition planarization of Hastelloy substrate for IBAD-MgO film | |
Liu et al. | Development of long REBCO coated conductors by PLD-REBCO/Sputter-CeO 2/IBAD-MgO at SJTU and SSTC | |
Arda et al. | Residual stress analysis of multi-layered buffer layers on Ni substrate for YBCO coated conductor | |
Li et al. | Fast growth processes of buffer layers for YBCO coated conductors on biaxially-textured Ni tapes | |
Lin et al. | Improved epitaxial texture of thick YBa2Cu3O7− δ/GdBa2Cu3O7− δ films with periodic stress releasing | |
JP5881107B2 (en) | Method for introducing nanoscale crystal defects into high temperature superconducting oxide thin films | |
Nie et al. | Biaxially textured MgO buffer layer on flexible metal template for coated conductor | |
Develos-Bagarinao et al. | Enhanced flux pinning in MOD YBa2Cu3O7− δ films by ion milling through anodic alumina templates | |
Chen et al. | Growth of biaxially textured CeO2/YSZ/CeO2 and SrTiO3 buffer layers on textured Ni substrates by pulsed laser deposition | |
Endo et al. | New growth approach of high-quality oxide thin films for future device applications: Independent control of supersaturation and migration | |
Araki et al. | Growth mechanism during firing process of single-coated thick YBCO films by TFA-MOD |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
AS | Assignment |
Owner name: LOS ALAMOS NATIONAL SECURITY, LLC, NEW MEXICO Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNORS:MATIAS, VLADIMIR;SHEEHAN, CHRISTOPHER J;SIGNING DATES FROM 20110921 TO 20110929;REEL/FRAME:027142/0879 |
|
AS | Assignment |
Owner name: U.S. DEPARTMENT OF ENERGY, DISTRICT OF COLUMBIA Free format text: CONFIRMATORY LICENSE;ASSIGNOR:LOS ALAMOS NATIONAL SECURITY;REEL/FRAME:027455/0739 Effective date: 20110906 |
|
AS | Assignment |
Owner name: SANDIA CORPORATION, NEW MEXICO Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNORS:IHLEFELD, JON FREDRICK;CLEM, PAUL GILBERT;SIGNING DATES FROM 20120809 TO 20120827;REEL/FRAME:028915/0131 |
|
STCB | Information on status: application discontinuation |
Free format text: ABANDONED -- FAILURE TO RESPOND TO AN OFFICE ACTION |